High strength austenitic stainless steel having excellent resistance to hydrogen embrittlement, method for manufacturing the same, and hydrogen equipment used for high-pressure hydrogen gas and liquid hydrogen environment

ABSTRACT

This high strength austenitic stainless steel having excellent resistance to hydrogen embrittlement includes, in terms of mass %, C: 0.2% or less, Si: 0.2% to 1.5%, Mn: 0.5% to 2.5%, P: 0.06% or less, S: 0.008% or less, Ni: 10.0% to 20.0%, Cr: 16.0% to 25.0%, Mo: 3.5% or less, Cu: 3.5% or less, N: 0.01% to 0.50%; and O: 0.015% or less, with the balance being Fe and unavoidable impurities, in which an average size of precipitates is 100 nm or less and an amount of the precipitates is 0.001% to 1.0% in terms of mass %.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a Divisional of copending application Ser. No.15/078,562, filed on Mar. 23, 2016, which claims priority under 35U.S.C. § 119(a) to Japanese Application No. 2015-064951, filed in Japanon Mar. 26, 2015, and Japanese Application No. 2016-057076, filed inJapan on Mar. 22, 2016, all of which are hereby expressly incorporatedby reference into the present application.

TECHNICAL FIELD

The present invention relates to a high strength austenitic stainlesssteel having excellent resistance to hydrogen embrittlement, a methodfor manufacturing the same, and a hydrogen equipment (application) usedfor (in) a high-pressure hydrogen gas and liquid hydrogen environment;and in particular, the present invention relates to a high strengthaustenitic stainless steel which is used for (in) a high-pressurehydrogen gas and liquid hydrogen environment and has excellentresistance to hydrogen embrittlement, and a method for manufacturing thesame.

BACKGROUND ART

In recent years, from a viewpoint of prevention of global warming, atechnology which utilizes hydrogen as a medium for transporting orstoring energy has been developed in order to suppress the emission ofgreenhouse gases (CO2, NON, and SON). Thus, development of a metalmaterial used for devices for transporting or storing hydrogen isexpected.

In the related art, a hydrogen gas having a pressure of about 40 MPa orlower as a high pressure gas is filled and stored in a gas cylinder madeof thick (thickness is large) Cr—Mo steel. In addition, as a pipingmaterial or a high-pressure hydrogen gas tank liner of a fuel-cellvehicle, a SUS316 type austenitic stainless steel (hereinafter, referredto as “SUS316 steel”) of the Japanese Industrial Standards is used. Theresistance to hydrogen embrittlement of the SUS316 steel in ahigh-pressure hydrogen gas environment is more satisfactory than thatof, for example, a carbon steel including the aforementioned Cr—Mo steelor SUS304 type austenitic stainless steel (hereinafter, referred to as“SUS304 steel”) of the Japanese Industrial Standards.

In recent years, prior to general sales of fuel-cell vehicles, anofficial trial production and a demonstration experiment of a hydrogenstation have been proceeded. For example, a hydrogen station is in thevalidation phase, and in the hydrogen station, a large amount ofhydrogen can be stored as liquid hydrogen and the pressure of the liquidhydrogen is increased to 70 MPa or higher to be supplied as ahigh-pressure hydrogen gas. In addition, in the hydrogen station, atechnology which is referred to as “precooling” has been put topractical use, and the technology “precooling” precools hydrogen whichis filled in a tank of the fuel-cell vehicle to a low temperature ofabout −40° C.

From the above-described matters, it is assumed that a metal materialused for a storage container for liquid hydrogen attached to a dispenserof the hydrogen station, a hydrogen gas piping, and the like is exposedto a hydrogen gas having a high pressure of 70 MPa and a lowtemperature.

As a metal material in which hydrogen embrittlement does not occur in anenvironment where hydrogen embrittlement occurs more severely, theSUS316 steel and SUS316L steel containing about 13% of Ni can beexemplified. Use of these two types of steels in a 70 MPa-class hydrogenstation in Japan is recognized in the exemplified standards determinedby the High Pressure Gas Safety Institute of Japan.

Meanwhile, in order to construct and autonomously develop a hydrogenenergy society where fuel-cell vehicles play leading rolls, it isessential to reduce the costs of fuel-cell vehicles and hydrogenstations. That is, with regard to the metal material used for a hydrogenembrittlement environment, in order to reduce the amount of the steelmaterial used, the size and thickness of various devices are reduced andthe strength of the metal material is required to be further increased.In particular, a tensile strength of about 650 MPa is required for themetal material used for a high-pressure hydrogen piping.

However, the SUS316 type austenitic stainless steel described in theaforementioned exemplified standards is expensive since the SUS316 typeaustenitic stainless steel includes a large amounts of Ni and Mo, whichare rare metals. However, even in the case where the SUS316 typeaustenitic stainless steel is subjected to a solution treatment, theSUS316 type austenitic stainless steel does not satisfy theabove-described tensile strength. Thus, the SUS316 type austeniticstainless steel is subjected to cold working to reinforce the strength,and then the SUS316 type austenitic stainless steel is used.

As the steel materials obtained by increasing the tensile strengths ofthe SUS316 steel and the SUS316L steel, the SUS316N and SUS316LN ofJapanese Industrial Standards steel types are known, and in these steeltypes, solid solution strengthening due to N is utilized. However, forexample, as reported in Non-Patent Document, ductilities of the SUS316Nand the SUS316LN are decreased in a high-pressure hydrogen gas at a lowtemperature.

With regard to a stainless steel disclosed in Patent Document 1(Japanese Unexamined Patent Application, First Publication No.2002-173742), the amount of Ni is set to be 4% to 12%, and athermomechanical treatment is conducted. Thereby, the metallographicstructure (microstructure) is controlled to be a dual-phasemicrostructure of an austenite phase and a martensite phase. As aresult, a remarkably hard stainless steel having a Vickers hardness ofabout 500 is achieved.

With regard to a stainless steel disclosed in Patent Document 2(Japanese Unexamined Patent Application, First Publication No.2009-133001), resistance to hydrogen embrittlement is enhanced byutilizing carbonitrides of Ti and Nb having sizes of 1 μm or more, andthe stainless steel is economically excellent since Mo is not added incontrast to the SUS316 steel.

However, since the stainless steel disclosed in Patent Document 1includes a martensite phase in which hydrogen embrittlement easilyoccurs, it is difficult to use this stainless steel in a hydrogenenvironment.

In addition, the strength of the stainless steel disclosed in PatentDocument 2 is in the same range of the strength of SUS316 steel, and itis desired that the strength thereof is further enhanced.

As such, currently, a high strength austenitic stainless steel havingresistance to hydrogen embrittlement in a low temperature andhigh-pressure hydrogen gas environment having a pressure of higher than40 MPa has not been appeared yet.

PRIOR ART DOCUMENTS Patent Documents

-   Patent Document 1: Japanese Unexamined Patent Application, First    Publication No. 2002-173742-   Patent Document 2: Japanese Unexamined Patent Application, First    Publication No. 2009-133001-   Patent Document 3: Japanese Unexamined Patent Application, First    Publication No. 2014-47409-   Patent Document 4: Japanese Unexamined Patent Application, First    Publication No. 2014-1422

Non-Patent Document

-   Non-Patent Document 1: “Effect of Temperature on Hydrogen    Environment Embrittlement of Type 316 Series Austenitic Stainless    Steels at Low temperatures”, Journal of the Japan Institute of    Metals and Materials, Vol. 67, No. 9, pp. 456 to 459

SUMMARY OF THE INVENTION

The present invention has been made in consideration of theaforementioned circumstances, and the present invention aims to providea high strength austenitic stainless steel having excellent resistanceto hydrogen embrittlement, which can be appropriately used in a lowtemperature and high-pressure hydrogen gas environment having a pressureof higher than 40 MPa.

For example, Patent Document 3 (Japanese Unexamined Patent Application,First Publication No. 2014-47409) discloses a stainless steel forhigh-pressure hydrogen aiming for increasing the strength byprecipitation strengthening.

The stainless steel disclosed in Patent Document 3 utilizes η phaseintermetallic compounds. However, it is necessary to add 20% or more ofNi and this causes an increase in alloy cost.

Therefore, the present inventors paid attention to Cr-basedcarbonitrides as precipitates obtainable by utilizing major elements.

Meanwhile, in general, various properties of the stainless steel aredegraded by the influence of the Cr-based carbonitrides. For example, asdisclosed in Patent Document 4 (Japanese Unexamined Patent Application,First Publication No. 2014-1422), in the case where the Cr-basedcarbonitrides are precipitated, an interface between the Cr-basedcarbonitride and a matrix phase becomes a starting point of fracture,and this causes degradation of formability.

Further, the influence of the Cr-based carbonitrides on the resistanceto hydrogen embrittlement of the stainless steel is not exceptional.According to Non-Patent Document 1, in the case where the Cr-basedcarbonitrides are precipitated in the metallographic structure(microstructure), a Cr-depletion layer in which the Cr concentration isremarkably decreased is formed in the surroundings of this precipitate.Since the stability of the austenite phase is decreased in the vicinityof this Cr-depletion layer, a deformation-induced martensite phase isgenerated preferentially at the time of deformation, and this causesdegradation in ductility in the high-pressure hydrogen gas. It ispossible to cause the Cr depletion layer to be disappeared byadditionally performing a heat treatment to diffuse Cr, but doing soincreases the manufacturing cost.

The present inventors have thoroughly studied the relationship betweenan alloy component composition of the austenitic stainless steelincluding Cr, Ni, and Mo, which are major elements, and trace elements,and a microstructure, the average size of the precipitates, resistanceto hydrogen embrittlement in a high-pressure hydrogen gas environment,and the strength characteristics. As a result, the following newfindings (a) to (f) are obtained.

(a) In the specimen where hydrogen embrittlement has occurred, cracksare generated in the surroundings of Cr-based carbonitrides andintermetallic compounds of Ni, Fe, Cr, Mo, and Si. As the cracksgenerated in the surroundings of these precipitates are linked to eachother and propagated, the ductility is decreased.

(b) However, by controlling the size of the precipitate to be 100 nm orless and controlling the amount thereof to be 1.0% or less in terms ofmass %, the generation and the development of the cracks which aregenerated by hydrogen embrittlement are remarkably suppressed, and as aresult, resistance to hydrogen embrittlement is enhanced.

(c) By controlling the average size of the precipitates to be 100 nm orless and controlling the amount of the precipitates to be 0.001% to 1.0%in terms of mass %, the precipitates such as Cr-based carbonitrides,intermetallic compounds of Ni, Fe, Cr, Mo, and Si, and Ti, Nb, andV-based carbonitrides act effectively on increasing the strength of theaustenitic stainless steel. Further, it is possible to obtain a tensilestrength of about 650 MPa, which is equal to or higher than that of thecold-worked material of SUS316 steel, by utilizing solid solutionstrengthening due to N and acting and combining precipitationstrengthening therewith.

(d) The size of the precipitate is greatly affected by heat treatmentconditions. The precipitation nose of the Cr-based carbonitrides and theintermetallic compounds of Ni, Fe, Cr, Mo, and Si is about 800° C., andin the case where a steel material is retained at a temperature ofhigher than 800° C., the precipitates are generated within a shortperiod of time, and the precipitates are rapidly coarsened. Thus, it isdifficult to control the average size of the precipitates to be 100 nmor less. In the case where a steel material is retained at a temperatureof 800° C. or lower, the coarsening of the precipitates can besuppressed but it takes time to start the precipitation.

(e) At the time of cooling after the final heat treatment, bycontrolling the average cooling rate to be less than 2.0° C./s until atemperature reaches 750° C., it is possible to secure the size and theamount in terms of mass % of the precipitates which attain both of theincrease in strength of the stainless and the enhancement of theresistance to hydrogen embrittlement.

(f) In addition, by adding one or more Ti, Nb, and V which easily formcarbonitrides to the steel material in a trace amount to precipitate theTi, Nb, and V-based carbonitrides, or by adding Cu to precipitate Cu, itis possible to further increase the strength without impairingresistance to hydrogen embrittlement.

The present invention has been made based on the aforementioned newfindings (a) to (f) and the features thereof are as follows.

(1) A high strength austenitic stainless steel having excellentresistance to hydrogen embrittlement includes, in terms of mass %, C:0.2% or less, Si: 0.2% to 1.5%, Mn: 0.5% to 2.5%, P: 0.06% or less, S:0.008% or less, Ni: 10.0% to 20.0%, Cr: 16.0% to 25.0%, Mo: 3.5% orless, Cu: 3.5% or less, N: 0.01% to 0.50%, and O: 0.015% or less, withthe balance being Fe and unavoidable impurities,

in which an average size of precipitates is 100 nm or less and an amountof the precipitates is 0.001% to 1.0% in terms of mass %.

(2) The high strength austenitic stainless steel having excellentresistance to hydrogen embrittlement according to (1), further includesone or more selected from the group consisting of, in terms of mass %,Al: 0.3% or less, Mg: 0.01% or less, Ca: 0.01% or less, REM: 0.10% orless, and B: 0.008% or less.(3) The high strength austenitic stainless steel having excellentresistance to hydrogen embrittlement according to (1) or (2), furtherincludes one or more selected from the group consisting of, in terms ofmass %, Ti: 0.5% or less, Nb: 0.5% or less, and V: 0.5% or less.(4) The high strength austenitic stainless steel having excellentresistance to hydrogen embrittlement according to any one of (1) to (3)is used for a high-pressure hydrogen gas and liquid hydrogenenvironment.(5) A method for manufacturing a high strength austenitic stainlesssteel having excellent resistance to hydrogen embrittlement, the methodincludes: subjecting a semi-finished product having a componentcomposition according to any one of (1) to (3) to hot working;performing a final heat treatment at a temperature of 1000° C. to 1200°C.; and performing cooling after the final heat treatment, in which, inthe cooling, an average cooling rate until a temperature reaches 750° C.is controlled to be less than 2.0° C./s.(6) A hydrogen equipment used for a high-pressure hydrogen gas andliquid hydrogen environment, in which the high strength austeniticstainless steel having excellent resistance to hydrogen embrittlementaccording to any one of (1) to (4) is used.

Effects of the Invention

According to one aspect of the present invention, it is possible toprovide a high strength austenitic stainless steel which has excellentresistance to hydrogen embrittlement and is appropriately used in ahigh-pressure hydrogen gas and liquid hydrogen environment, and a methodfor manufacturing the same.

EMBODIMENTS FOR CARRYING OUT THE INVENTION

Hereinafter, the austenitic stainless steel and the method formanufacturing thereof according to the embodiment will be described indetail.

First, the component composition of the austenitic stainless steelaccording to the embodiment will be described. In addition, in thefollowing description, the “%” indicating the amount of each elementmeans “mass %”.

The austenitic stainless steel according to the embodiment includes, interms of mass %, C: 0.2% or less, Si: 0.2% to 1.5%, Mn: 0.5% to 2.5%, P:0.06% or less, S: 0.008% or less, Ni: 10.0% to 20.0%, Cr: 16.0% to25.0%, Mo: 3.5% or less, Cu: 3.5% or less, N: 0.01% to 0.50%, and O:0.015% or less. Further, the average size of the precipitates is 100 nmor less, and the amount of the precipitates is 0.001% to 1.0% in termsof mass %.

<C: 0.2% or Less>

C is an element effective for stabilizing an austenite phase and Ccontributes to enhancing resistance to hydrogen embrittlement. Inaddition, C also contributes to an increase in strength due to solidsolution strengthening and precipitation strengthening due to Cr-basedcarbides. In order to obtain these effects, it is preferable to set theamount of C to be 0.01% or more. Meanwhile, an excessive amount of Ccauses precipitation of an excessive amount of Cr-based carbides andthis leads to degradation of resistance to hydrogen embrittlement.Therefore, it is necessary to set the upper limit of the amount of C tobe 0.2%. The upper limit of the amount of C is more preferably 0.15%.

<Si: 0.2% to 1.5%>

Si is an element effective for stabilizing the austenite phase. It isnecessary to set the amount of Si to be 0.2% or more in order to enhanceresistance to hydrogen embrittlement by stabilizing the austenite phase.The amount of Si is preferably 0.4% or more. Meanwhile, an excessiveamount of Si promotes generation of intermetallic compounds such as asigma phase and the like and this causes degradation of hot workabilityand toughness. Therefore, it is necessary to set the upper limit of theamount of Si to be 1.5%. The amount of Si is more preferably 1.1% orless.

<Mn: 0.5% to 2.5%>

Mn is an element effective for stabilizing the austenite phase. Thestabilization of the austenite phase suppresses generation ofdeformation-induced martensite phase; and thereby, resistance tohydrogen embrittlement is enhanced. Therefore, it is necessary to setthe amount of Mn to be 0.5% or more. The amount of Mn is preferably 0.8%or more.

Meanwhile, an excessive amount of Mn promotes generation of coarse MnSinclusions and this causes degradation in ductility of the austenitephase. In addition, an excessive amount of Mn also has an action ofpromoting generation of nitrides. Therefore, it is necessary to set theupper limit to be 2.5%. The amount of Mn is more preferably 2.0% orless.

<P: 0.06% or Less>

P is included as an impurity in the austenitic stainless steel of theembodiment. Since P is an element degrading hot workability, it ispreferable to reduce the amount of P as much as possible. Specifically,it is preferable to limit the amount of P to be 0.06% or less and ismore preferable to limit the amount thereof to be 0.05% or less.However, since an extreme reduction in the amount of P leads to anincrease in the production cost of the steel, the amount of P ispreferably 0.008% or more.

<S: 0.008% or Less>

S is an element which is segregated in austenite grain boundaries at thetime of hot working and S weakens the bonding strength of the grainboundary. Thereby, S induces cracks at the time of hot working.Therefore, it is necessary to limit the upper limit of the amount of Sto be 0.008%. The upper limit of the amount of S is preferably 0.005%.Since it is preferable to reduce the amount of S as much as possible,the lower limit is not particularly provided; however, an extremereduction in the amount of S leads to an increase in the production costof the steel. Therefore, the amount of S is preferably 0.0001% or more.

<Ni: 10.0% to 20.0%>

Ni is an element which is very effective for enhancing resistance tohydrogen embrittlement of the austenitic stainless steel. In addition,Ni promotes generation of intermetallic compounds of Ni, Fe, Cr, Mo, andSi and Ni contributes to increasing the strength. In order to obtainthese effects, it is necessary to set the amount of Ni to be 10.0% ormore. Since these effects are further enhanced by homogenizing thecomponent segregation, the amount of Ni is preferably 11.5% or more.Meanwhile, since an excessive amount of Ni causes an increase inmaterial cost, the upper limit of the amount of Ni is set to be 20.0%.The amount of Ni is preferably 14.0% or less.

<Cr: 16.0% to 25.0%>

Cr is an indispensable element for obtaining corrosion resistancerequired for a stainless steel. In addition, Cr is an elementcontributing to an increase in strength of the austenitic stainlesssteel. In order to obtain these effects, it is necessary to set theamount of Cr to be 16.0% or more. The amount of Cr is preferably 16.5%or more. Meanwhile, an excessive amount of Cr causes precipitation of anexcessive amount of Cr-based carbonitrides and this degrades resistanceto hydrogen embrittlement. Therefore, it is necessary to set the upperlimit of the amount of Cr to be 25.0%. The amount of Cr is preferably22.5% or less.

<Mo: 3.5% or Less>

Mo is an element contributing to an increase in strength of theaustenitic stainless steel and enhancement of the corrosion resistance.However, an addition of Mo causes an increase in the alloy cost.Therefore, the amount of Mo is set to be 3.5% or less. Meanwhile, Mo isan element which is unavoidably mixed in from a scrap material. Anextreme reduction in the amount of Mo causes restriction of adissolution material and this leads to an increase in manufacturingcost. Therefore, in order to obtain the aforementioned effect andmanufacturability, it is preferable to set the lower limit of the amountof Mo to be 0.05%.

<Cu: 3.5% or Less>

Cu is an element effective for stabilizing the austenite phase. Sincestabilization of the austenite phase enhances resistance to hydrogenembrittlement, the amount of Cu is preferably 0.15% or more. Meanwhile,Cu contributes to an increase in strength due to precipitationstrengthening due to Cu; however, an excessive amount of Cu leads to adecrease in strength of the austenite phase and also impairs hotworkability. Therefore, it is necessary to set the upper limit of theamount of Cu to be 3.5%. The amount of Cu is more preferably 3.0% orless.

<N: 0.01% to 0.50%>

N is an element effective for stabilizing an austenite phase andenhancing corrosion resistance. In addition, N also contributes to anincrease in strength due to solid solution strengthening andprecipitation strengthening due to Cr-based nitrides. In order to obtainthese effects, the amount of N is set to be 0.01% or more. The amount ofN is preferably 0.04% or more. Meanwhile, an excessive amount of Npromotes generation of an excessive amount of Cr-based nitrides, andthis degrades resistance to hydrogen embrittlement of the austenitephase, corrosion resistance, and toughness. Therefore, it is necessaryto set the upper limit of the amount of N to be 0.50%. The amount of Nis more preferably 0.35% or less.

<O: 0.015% or Less>

O forms oxides in the steel; and thereby, O degrades hot workability andtoughness of the austenite phase. Therefore, it is necessary to limitthe upper limit of the amount of O (oxygen) to be 0.015% or less. Theamount of O is preferably 0.010% or less. It is preferable to reduce theamount of O (oxygen) as much as possible, but an extreme reduction inthe amount thereof leads to an increase in the production cost of thesteel. Therefore, the amount of O (oxygen) is preferably 0.001% or more.

The austenitic stainless steel according to the embodiment includes Feand unavoidable impurities in addition to the elements which have beendescribed above. However, the austenitic stainless steel may containoptionally added elements which are described below.

<Al: 0.3% or Less, Mg and Ca: 0.01% or Less, REM: 0.10% or Less, and B:0.008% or Less>

Al, Mg, Ca, REM, and B are elements effective for deoxidization andenhancement of hot workability and corrosion resistance. If necessary,one or more elements selected from these may be added. However,excessive amounts of these elements cause a remarkable increase in themanufacturing cost. Therefore, it is necessary to set the upper limitsof the amounts of these elements to be Al: 0.3% or less, Mg and Ca:0.01% or less, REM: 0.10% or less, and B: 0.008% or less. It is notnecessary to provide the lower limits of the amounts of these elementsin particular; however, in order to sufficiently obtain thedeoxidization effect, it is preferable to set the lower limits to be Al:0.01%, Mg and Ca: 0.0002%, REM: 0.001%, and B: 0.0002%. Here, REM (rareearth element) refers to a generic term for 2 elements of scandium (Sc)and yttrium (Y), and 15 elements (lanthanoid) from lanthanum (La) tolutetium (Lu) according to the general definition. A single element maybe added or two or more elements may be added. The amount of REM is thetotal amount of these elements.

<Ti, Nb, and V: 0.50% or Less>

Ti, Nb, and V are solid-solubilized in the steel or precipitated ascarbonitrides; and thereby, the strength is increased. Therefore, Ti,Nb, and V are elements effective for increasing the strength. One ormore elements selected from these may be added as necessary. In thiscase, each of the amounts of Ti, Nb, and V is preferably 0.01% or more.However, in the case where each of the amounts of Ti, Nb, and V isincreased to more than 0.50%, generation of Cr-based carbonitrides issuppressed, and it is not possible to sufficiently obtain the effect ofprecipitation strengthening due to the Cr-based carbonitrides.Therefore, it is necessary to set the upper limit of each of the amountsof Ti, Nb, and V to be 0.50% or less. The upper limit of each of theamounts of Ti, Nb, and V is preferably 0.40%.

Other elements excluding the elements described above can be includedwithin the range not impairing the effects of the embodiment.

“Reasons for the Limitation Regarding Precipitates”

Next, the size and the generation amount of the precipitates in thesteel will be described.

In the specimen where hydrogen embrittlement has occurred, cracks aregenerated in the surroundings of Cr-based carbonitrides or intermetalliccompounds of Ni, Fe, Cr, Mo, and Si. This is because resistance tohydrogen gas embrittlement is locally degraded in the surroundings ofeach precipitate, which is caused by the Cr-depletion layer formed inthe surroundings of each precipitate. The cracks generated from thesurroundings of the precipitates as starting points are linked to eachother and propagated. Thus ductility is decreased.

However, by controlling the average size of the precipitates to be 100nm or less and controlling the generation amount of the precipitates tobe 1.0% or less in terms of mass %, generation and development of thecracks generated by hydrogen gas embrittlement are remarkablysuppressed. As a result, the resistance to hydrogen gas embrittlement isenhanced.

Further, in the case where the strength is increased by precipitationstrengthening due to the precipitates and solid solution strengtheningdue to N is acted and combined therewith, it is possible to obtain atensile strength of about 650 MPa, which is equal to or higher than thatof the cold-worked material of SUS316 steel. In order to obtain theseeffects, the lower limit of the generation amount of the precipitates isset to be 0.001% or more. The lower limit of the generation amount ofthe precipitates is preferably 0.005% or more.

The average size of the precipitates and the generation amount of theprecipitates can be controlled by controlling the average cooling rateafter the final heat treatment described below. The lower this averagecooling rate is, the more the precipitates are coarsened. Therefore, thepresence of the precipitates can be confirmed by a Transmission ElectronMicroscope (TEM). The average size of the precipitates is preferably 70nm or less.

Meanwhile, in the case where the average cooling rate is high (the casewhere the average cooling rate is close to the upper limit), theprecipitates are very fine. Therefore, the lower limit of the averagesize of the precipitates is not particularly provided, but is preferably5 nm or more.

The generation amount of carbonitrides and intermetallic compounds(precipitates) can be measured by, for example, an electroextractionresidual method.

In the case where an excessive amount of the precipitates are produced,linking and propagation of the cracks generated from the surroundings ofthe precipitates as starting points are promoted. Therefore, it isnecessary to set the generation amount of the precipitates to be 1.0% orless in terms of mass %. The generation amount of the precipitates ispreferably 0.90% or less in terms of mass %. Meanwhile, in the casewhere the cooling rate is high (the case where the cooling rate is closeto the upper limit), the precipitates are very fine. Therefore, thelower limit of the average size of the precipitates is not particularlyprovided. However, in order to obtain the effect of increasing thestrength due to Cr-based carbonitrides and intermetallic compounds ofNi, Fe, Cr, Mo, and Si, the generation amount is preferably 0.02% ormore in terms of mass %.

In addition, the average size of the precipitates is measured by, forexample, the following method. The precipitates are observed by TEM, theprecipitates are identified by EDX, and the precipitates are specified.Next, the major axis and the minor axis of one precipitate are measuredby a TEM photograph. Then, the average value of the major axis and theminor axis ((major axis+minor axis)/2) is calculated, and the averagevalue is utilized as the size of the precipitate. In the same manner,the sizes of a plurality of precipitates are obtained. The average valueof the sizes of the plurality of precipitates is calculated, and theaverage value thereof can be utilized as the average size of theprecipitates in the stainless steel. In addition, in the embodiment, arectangle circumscribing one precipitate is drawn such that the areathereof becomes the smallest. Then, the long side of this circumscribingrectangle is utilized as a major axis of the precipitate and the shortside of this circumscribing rectangle is utilized as a minor axis of theprecipitate.

In addition, the “precipitate” in the invention means all theprecipitates precipitated in the steel and includes Ti-, Nb-, andV-based carbonitrides, precipitated Cu, and the like in addition toCr-based carbonitrides and intermetallic compounds of Ni, Fe, Cr, Mo,and Si.

“Manufacturing Method”

Next, one example of the method for manufacturing an austeniticstainless steel according to the embodiment will be described.

For manufacturing the austenitic stainless steel of the embodiment, atfirst, a stainless steel having the aforementioned component compositionis melted to manufacture a semi-finished product such as a slab or thelike. Next, the semi-finished product is heated at a predeterminedtemperature, and the semi-finished product is subjected to hot workingsuch as hot rolling, or the like (a step of hot working).

The austenitic stainless steel of the embodiment is not limited to asteel sheet. Therefore, the semi-finished product is not limited to aslab, and it is needless to say that the austenitic stainless steel ofthe embodiment can be achieved by selecting a preferable shape of thesemi-finished product (billet, bloom, or the like) in accordance withthe shape of the target product (bar, pipe, or the like).

Hereinafter, conditions of the final heat treatment after the hotworking will be described in detail.

If the temperature of the final heat treatment after the hot working istoo high, the case may occur in which the strength of the steel materialis decreased due to excessive growth of grains. In addition, the casemay occur in which a grinding step is required to be further conductedbecause of the occurrence of abnormal oxidation, and this causes anincrease in the production cost. Therefore, the upper limit of thetemperature of the final heat treatment is set to be 1200° C. Meanwhile,if the temperature of the final heat treatment is too low, a deformationstructure formed in the hot working remains and ductility of a steelproduct is decreased. Therefore, the lower limit is set to be 1000° C.The temperature range of the final heat treatment is preferably 1050° C.to 1180° C.

The retention time (holding time) of the heat treatment in theaforementioned temperature range is set to be 1 second to 1 hour. If theretention time is shorter than the range, a worked structure remains inthe steel, and this causes a decrease in ductility. The lower limit ofthe retention time is preferably 30 seconds. In addition, if theretention time of the heat treatment is too long, the case may occur inwhich the strength is decreased due to excessive growth of grains. Inaddition, the case may occur in which a grinding step is required to befurther conducted because of the occurrence of abnormal oxidation, andthis causes an increase in the production cost. Therefore, the upperlimit of the retention time is set to be 40 minutes.

The precipitation nose temperature of Cr-based carbonitrides andintermetallic compounds of Ni, Fe, Cr, Mo, and Si is about 800° C. Inthe case where the steel material is retained at a temperature of higherthan this temperature, the precipitates are rapidly coarsened. Thus, itis difficult to control the average size of the precipitates to be 100nm or less. Meanwhile, in the case where the steel material is retainedat a temperature of 800° C. or lower, the coarsening of the precipitatescan be suppressed but it takes time to start the precipitation.Therefore, this leads to an increase in the manufacturing cost.

However, by controlling the average cooling rate to be less than 2.0°C./s until a temperature reaches 750° C. after the final heat treatmentat a temperature of 1000° C. to 1200° C., it is possible to secure theaverage size and the generation amount of the precipitates which attainboth of the increase in strength of the stainless steel and theenhancement of resistance to hydrogen embrittlement.

From the above-described matters, in the cooling step after the finalheat treatment, it is necessary to control the average cooling rate tobe less than 2.0° C./s until a temperature reaches 750° C. In the casewhere the average cooling rate is higher than 2.0° C./s, the time forwhich the precipitates are precipitated cannot be secured. Thus, it isnot possible to increase the strength of the steel product. Meanwhile,in the case where the cooling rate is excessively low, the average sizeof the precipitates may be more than 100 nm and satisfactory resistanceto hydrogen embrittlement of the steel product may not be secured.Therefore, the lower limit of the average cooling rate is preferably0.3° C./s or higher. The lower limit is more preferably 0.4° C./s orhigher.

In addition, after the aforementioned hot working and final heattreatment are performed, acid washing or cold working may be conductedas necessary.

In addition, the method for manufacturing the austenitic stainless steelaccording to the embodiment is not limited to the manufacturing methoddescribed above, and any manufacturing method may be adopted, if themethod is a method by which the average size and the generation amountof the precipitates can be controlled within the aforementioned ranges.

In addition, the average size and the generation amount of theprecipitates may be controlled within the aforementioned ranges by aheat treatment in a step of manufacturing a hydrogen equipment(application) in which the austenitic stainless steel including thecomponents within the ranges of the invention is used, or a heattreatment to which the hydrogen equipment (application) is subjected.

Examples

Examples of the invention will be described in detail, but the inventionis not limited to conditions used in the following Examples.

In addition, the underlined values in Tables indicate that they are outof the ranges of the embodiment.

A stainless steel test material having a component composition shown inTable 1 was melted, and a semi-finished product having a thickness of120 mm was manufactured. Next, the semi-finished product was heated at atemperature of 1200° C., and then the semi-finished product wassubjected to hot forging and hot rolling to obtain a hot-rolled sheethaving a thickness of 20 mm. Next, the hot-rolled sheet was subjected toa final heat treatment and cooling under conditions shown in Table 2 toobtain a hot-rolled and annealed sheet. The retention time for the finalheat treatment was 3 minutes to 20 minutes. The “heat treatmenttemperature (° C.)” in Table 2 indicates the temperature of the finalheat treatment, and the “cooling rate (° C./s)” indicates the averagecooling rate until the temperature reached 750° C.

The average size of the precipitates and the amount of the precipitatesof each test material are shown in Table 2.

A sample was formed from the obtained hot-rolled and annealed sheet byan extraction replica method, and then the precipitates were observed bya TEM. The size of one precipitate was determined as the average valueof the major axis and the minor axis ((major axis+minor axis)/2). Thesizes of 30 precipitates were measured, and the average value of thesizes of the 30 precipitates was determined to be the average size ofthe precipitates in the test material.

An analysis sample was collected from the test material in the samemanner, and the amount of the precipitates was measured according to theelectroextraction residual method. A filter having a mesh size of 0.2 μmwas used as the filter for filtering out a residue.

Next, with regard to each hot-rolled and annealed sheet of the testmaterial, the resistance to hydrogen gas embrittlement was evaluatedaccording to the method shown below.

A round bar tensile specimen which included a parallel part having anouter diameter of 3 mm and a length of 20 mm was collected from alongitudinal direction of the hot-rolled and annealed sheet having athickness of 20 mm and a central part of the sheet thickness. (1) Atensile test in the atmosphere and (2) a tensile test in thehigh-pressure hydrogen gas were performed using this round bar tensilespecimen.

The tensile test (1) in the atmosphere was conducted under conditions inwhich the test temperatures were 25° C. and −40° C. and the strain ratewas 5×10⁻⁵/s. A specimen of which the tensile strength measured by thetensile test at 25° C. was higher than 650 MPa was evaluated as “Pass”(acceptable quality).

The tensile test (2) in the high-pressure hydrogen gas was conductedunder conditions in which the test temperature was −40° C., the testenvironment was a hydrogen gas of 70 MPa, and the strain rate was5×10⁻⁵/s. The specimen Nos. A3, A4, and A6 were also subjected to thetensile test under conditions in which the test environment was ahydrogen gas of 103 MPa in the same manner as described above except fortest environment.

Then, the value (relative reduction of area) of “(reduction of the areain the high-pressure hydrogen gas/reduction of the area in theatmosphere)×100(%)” at −40° C. was calculated. A test material havingthe value of 80% or more was evaluated such that the resistance tohydrogen embrittlement in the high-pressure hydrogen gas was “Pass”(acceptable quality). In particular, a specimen in which the tensilestrength at 25° C. was higher than 650 MPa and the reduction of area was80% or more and less than 85% was evaluated as “◯”, and a specimen inwhich the tensile strength at 25° C. was higher than 650 MPa and thereduction of area was 85% or more was evaluated as “A”.

The results are shown in Table 3 and Table 4.

The specimens A1a, A1c, and A2 to A18 are test materials (InventionExamples) which were subjected to the final heat treatment and thecooling under preferable conditions.

With regard to these specimens, the tensile strengths at 25° C. in theatmosphere were 650 MPa or higher, while the relative reduction of areavalues (the values of the relative reduction of area) were 80% or more.In particular, with regard to the specimens Ala, A2 to A6, and A8 to A17in which the amounts of Ni and Cu having great influences on enhancingthe resistance to hydrogen embrittlement and the average cooling ratewere within the preferable ranges of the embodiment, the relativereduction of area values were 85% or more, and the resistances tohydrogen embrittlement were excellent.

In addition, the specimens A3, A4, and A6 were also subjected to thetensile test in the hydrogen gas of 103 MPa, and the relative reductionsof area were 90% or more which were more than the target value of 80%.

With regard to the specimen Alb, the cooling rate after the final heattreatment was out of the range of the invention. As a result, theprecipitates were not precipitated in the test material during thecooling after the final heat treatment and the effect of precipitationstrengthening could not be obtained. Thus, the tensile strength in theatmosphere at room temperature was lower than 650 MPa.

With regard to the specimen B1, the amount of Ni was less than the rangeof the invention. As a result, the resistance to hydrogen embrittlementwas insufficient and the relative reduction of area value was 59%.

With regard to the specimen B2, the amount of Cu was more than the rangeof the invention. As a result, the strength of the austenite phase wasdecreased and the tensile strength at 25° C. in the atmosphere was lowerthan the target value of 650 MPa.

With regard to the specimen B3, the amount of Si was more than the rangeof the invention. As a result, the resistance to hydrogen embrittlementwas insufficient and the relative reduction of area value was 68.8%.

With regard to the specimen B4, the amount of Cr was more than the rangeof the invention. As a result, the precipitates were precipitated at anamount of more than the range of the invention. Consequently, thehydrogen gas embrittlement sensitivity was increased, the resistance tohydrogen embrittlement was insufficient, and the relative reduction ofarea value was 61.5%.

With regard to the specimen B5, the amount of Mn was more than the rangeof the invention. As a result, the resistance to hydrogen embrittlementwas insufficient and the relative reduction of area value was 71.3%.

With regard to the specimen B6, the amount of Cr was less than the rangeof the invention. As a result, the stability of the austenite phase wasdecreased; and thereby, the resistance to hydrogen embrittlement wasinsufficient and the relative reduction of area value was 77.5%.

With regard to the specimen B7, the amount of N was less than the rangeof the invention. As a result, the strength of the austenite phase wasdecreased and the tensile strength at 25° C. in the atmosphere was lowerthan the target value of 650 MPa.

TABLE 1 Steel Component Composition (mass %) No. C Si Mn P S Ni Cr Mo CuN O Others Remarks A1 0.09 0.49 0.66 0.037 0.005 12.9 18.4 2.2 0.22 0.220.009 Invention A2 0.08 0.49 0.81 0.030 0.004 12.8 18.4 2.2 0.31 0.130.008 steel A3 0.15 0.48 0.79 0.034 0.004 13.1 17.9 2.1 0.25 0.26 0.009A4 0.10 0.50 0.93 0.036 0.005 14.4 18.8 2.2 0.22 0.23 0.011 A5 0.11 1.110.50 0.036 0.004 15.0 19.0 2.4 0.23 0.23 0.007 A6 0.06 0.49 2.10 0.0350.003 18.3 23.8 1.9 1.52 0.44 0.009 A7 0.09 0.51 0.64 0.037 0.003 10.919.1 2.1 2.93 0.25 0.009 A8 0.08 0.49 0.72 0.042 0.005 12.6 16.9 2.30.24 0.19 0.008 A9 0.09 0.49 0.92 0.037 0.004 12.6 18.3 3.3 0.22 0.220.008 A10 0.11 0.55 0.82 0.025 0.005 13.0 18.1 0.8 0.25 0.05 0.007A1:0.067, Ca:0.0031, B:0.0019 A11 0.10 0.51 1.11 0.034 0.004 12.9 18.01.8 0.29 0.22 0.009 Mg:0.0042, Ca:0.0021 A12 0.11 0.49 1.14 0.033 0.00512.8 18.4 1.9 0.22 0.24 0.009 REM:0.008 A13 0.09 0.51 0.87 0.037 0.00513.0 18.1 2.0 0.23 0.21 0.007 Ti:0.12, Nb:0.09, V:0.11 A14 0.09 0.490.96 0.031 0.004 12.9 17.8 2.0 0.23 0.28 0.007 Ti:0.21 A15 0.14 0.320.68 0.033 0.003 13.1 17.6 2.1 0.28 0.25 0.009 Nb:0.18 A16 0.10 0.510.82 0.033 0.005 13.0 18.0 2.4 0.20 0.25 0.012 V:0.22 A17 0.06 0.40 1.090.016 0.003 14.1 18.7 2.2 0.23 0.39 0.008 A1:0.059, Ca:0.0033, Ti:0.14,Nb:0.15 A18 0.03 0.41 1.0 0.031 0.004 12.3 17.8 1.7 0.09 0.13 0.004 B10.11 0.45 0.65 0.037 0.004 8.5 18.1 1.9 0.22 0.23 0.009 Comparative B20.12 0.49 0.65 0.039 0.005 12.5 18.0 1.9 4.11 0.25 0.006 A1:0.055,Ca:0.0038, B:0.0011 steel B3 0.10 3.10 0.6 0.034 0.005 12.6 18.7 2.00.21 0.24 0.009 B4 0.09 0.50 0.61 0.029 0.005 13.1 27.4 1.9 0.24 0.310.009 B5 0.12 0.49 3.2 0.051 0.004 12.9 18.2 2.1 0.28 0.63 0.010 B6 0.110.44 0.87 0.035 0.003 12.0 14.2 1.8 0.29 0.14 0.009 B7 0.01 0.49 0.810.032 0.004 12.5 17.6 2.4 0.22 0.008 0.006 Ti:0.10, Nb:0.08, V:0.08

TABLE 2 Size of Amount of Specimen Heat treatment Cooling precipitatesprecipitates No. temperature (° C.) rate (° C./s) (nm) (mass %) RemarksA1 A1a 1080 1.5 15 0.170 Invention Example A1b 1080 7.0 Precipitateswere not detected Comparative Example A1 c 1080 0.3 85 0.205 InventionA2 1080 1.5 10 0.023 Example A3 1080 1.5 15 0.217 A4 1100 1.5 20 0.470A5 1100 1.5 20 0.122 A6 1080 1.8 30 0.571 A7 1080 1.8 30 0.142 A8 11501.5 20 0.277 A9 1150 1.5 20 0.660 A10 1150 1.5 20 0.131 A11 1080 1.5 200.188 A12 1080 1.5 15 0.158 A13 1080 1.5 20 0.113 A14 1100 1.8 25 0.136A15 1100 1.8 25 0.141 A16 1100 1.8 20 0.151 A17 1100 1.8 35 0.440 A181100 1.8 20 0.143 B1 1080 1.8 20 0.177 Comparative B2 1080 1.8 30 0.258Example B3 1100 1.5 30 0.336 B4 1100 1.5 20 1.328 B5 1100 1.5 25 1.584B6 1080 1.5 20 0.110 B7 1080 1.8 15 0.020

TABLE 3 Tensile Reduction of area, −40° C. Relative Specimen strengthAtmosphere Hydrogen of reduction of No. 25° C. (MPa) (%) 70 MPa (%) area(%) Evaluation Remarks A1 A1a 712 79 73 92.4 @ Invention Example A1b 59082 70 85.4 x Comparative Example A1c 660 76 61 80.3 ∘ Invention A2 68184 81 96.4 @ Example A3 709 80 74 92.5 @ A4 776 74 77 104.1 @ A5 701 7977 97.5 @ A6 710 84 86 102.4 @ A7 664 79 65 82.3 ∘ A8 706 77 75 97.4 @A9 729 80 72 90.0 @ A10 701 82 73 89.0 @ A11 707 79 76 96.2 @ A12 720 7870 89.7 @ A13 703 75 68 90.7 @ A14 706 77 71 92.2 @ A15 721 81 75 92.6 @A16 702 79 68 86.1 @ A17 711 78 77 98.7 @ A18 725 77 62 80.5 ∘ B1 711 7846 59.0 x Comparative B2 616 83 68 81.9 x Example B3 713 77 53 68.8 x B4755 78 48 61.5 x B5 749 80 57 71.3 x B6 716 80 62 77.5 x B7 619 77 6381.8 x

TABLE 4 Reduction of area, −40° C. Relative Specimen Atmosphere Hydrogenof 103 reduction No. (%) MPa (%) of area (%) Remarks A3 81 79 97.5Invention A4 77 73 94.8 Example A6 72 75 104.2

INDUSTRIAL APPLICABILITY

The austenitic stainless steel of the invention has extremely excellentresistance to hydrogen embrittlement in a high-pressure hydrogen gashaving a pressure of higher than 40 MPa, and a tensile strength ofhigher than 650 MPa. Therefore, the austenitic stainless steel of thepresent invention can be applied as materials of a high-pressurehydrogen gas tank for storing a hydrogen gas having a pressure of higherthan 40 MPa, a high-pressure hydrogen gas tank liner, a high-pressurehydrogen gas heat exchanger, and a piping for a high-pressure hydrogengas and liquid hydrogen.

1. A hydrogen equipment used for a high-pressure hydrogen gas and liquidhydrogen environment, in which an austenitic stainless steel havingresistance to hydrogen embrittlement is used, wherein the austeniticstainless steel having resistance to hydrogen embrittlement comprises,in terms of mass %: C: 0.2% or less; Si: 0.2% to 1.5%; Mn: 0.5% to 2.5%;P: 0.042% or less; S: 0.008% or less; Ni: 10.0% to 20.0%; Cr: 16.0% to19.1%; Mo: 3.5% or less; Cu: 1.52% or less; N: 0.01% to 0.50%; and O:0.015% or less, with a balance being Fe and unavoidable impurities,wherein an average size of precipitates is 100 nm or less and an amountof the precipitates is 0.001% to 1.0% in terms of mass %.
 2. Thehydrogen equipment used for a high-pressure hydrogen gas and liquidhydrogen environment according claim 1, wherein the austenitic stainlesssteel having resistance to hydrogen embrittlement further comprises oneor more selected from the group consisting of, in terms of mass %, Al:0.3% or less, Mg: 0.01% or less, Ca: 0.01% or less, REM: 0.10% or less,and B: 0.008% or less.
 3. The hydrogen equipment used for ahigh-pressure hydrogen gas and liquid hydrogen environment accordingclaim 1, wherein the austenitic stainless steel having resistance tohydrogen embrittlement further comprises one or more selected from thegroup consisting of, in terms of mass %, Ti: 0.5% or less, Nb: 0.5% orless, and V: 0.5% or less.
 4. The hydrogen equipment used for ahigh-pressure hydrogen gas and liquid hydrogen environment accordingclaim 2, wherein the austenitic stainless steel having resistance tohydrogen embrittlement further comprises one or more selected from thegroup consisting of, in terms of mass %, Ti: 0.5% or less, Nb: 0.5% orless, and V: 0.5% or less.